Precursor-Mediated Colloidal Synthesis of Compositionally Tunable Cu–Sb–M–S (M = Zn, Co, and Ni) Nanocrystals and Their Transport Properties

The solution-based colloidal synthesis of multinary semiconductor compositions has allowed the design of new inorganic materials impacting a large variety of applications. Yet there are certain compositions that have remained elusive—particularly quaternary structures of transition metal-based (e.g., Co, Zn, Ni, Fe, Mn, and Cr) copper antimony chalcogenides. These are widely sought for tuning the electrical and thermal conductivity as a function of the size, composition, and crystal phase. In this work, a facile hot injection approach for the synthesis of three different tetrahedrite-substituted nanocrystals (NCs) (Cu10Zn2Sb4S13, Cu10Co2Sb4S13, and Cu10Ni1.5Sb4S13) and their growth mechanisms are investigated. We reveal that the interplay between the Zn, Ni, and Co precursors on the basis of thiophilicity is key to obtaining pure phase NCs with controlled size and shape. While all of the synthesized crystal phases display outstanding low thermal conductivity, the Cu10.5Sb4Ni1.5S13 system shows the most enhanced electrical conductivity compared to Cu10Zn2Sb4S13 and Cu10Co2Sb4S13. This study highlights an effective synthesis strategy for the growth of complex quaternary nanocrystals and their high potential for application in thermoelectrics.


INTRODUCTION
Copper-based multinary colloidal nanocrystals (NCs) comprising low hazardous and earth-abundant elements are important due to their composition and size-tunable bandgap combined with their high light absorption coefficient, which make them relevant for electrocatalysis, photovoltaics, and thermoelectrics. 1−7 The colloidal hot injection method has emerged as one of the most adaptable bottom-up synthesis techniques for tailoring the structure−property relationship of colloidal NCs for various applications with respect to the composition, size, shape, crystal phase, and cation or anion ratios. 3,7−17 While extending this hot injection strategy to multinary copper-based chalcogenides is challenging due to the additional metal cations, many successful protocols have been reported for tuning composition in a wide variety of I−III−VI (CIS, CISe, and CIGSe) and I−IV−VI (CZTS and CZTSe) systems. 18−21 Recently, Cu−Sb−S systems have gained interest, particularly due to the complexity of the crystal phases and potential opportunities to tune their thermal and electrical conductivity based on the crystal structure, shape, and size of nanocrystals. 22−26 Four crystallographic phases of the Cu−Sb−S system exist, including tetrahedrite (Cu 12 Sb 4 S 13 ), chalcostibite (CuSbS 2 ), skinnerite (Cu 3 SbS 3 ), and fematinite (Cu 3 SbS 4 ). Among these phases, tetrahedrite, due to its naturally low-lattice thermal conductivity, is a promising alternative material for thermoelectric applications. Tetrahedrite with the chemical formula (Cu + ) 10 (Cu 2+ ) 2 Sb 4 S 13 has both Cu(I) and Cu(II) ions in the crystal structure. Metal cations in the crystal structure of tetrahedrite with oxidation states +1, +2, and +3 allow versatility in the inclusion of various isovalent dopants. Optimum thermoelectric, optical, and magnetic properties require the partial substitution of other elements by the replacement of Cu, Sb, and chalcogen sites in Cu 12−x A x Sb 4−y B y S 13−z Se z (A = M 2+ ; B = M 3+ ). 27,28 Substituted tetrahedrites are usually synthesized by solid-state reactions, which typically need longer reaction times (>30 h) and high reaction temperatures (>850°C) to obtain highquality bulk materials. 29,30 In contrast, a limited number of approaches are reported with a solution-based synthetic approach. This includes solution-based polyol processes for the synthesis of pure and substituted tetrahedrite (50−200 nm) using reducing agents such as NaBH 4 . 31−34 The fast injection of single source precursors followed by rapid cooling was also observed to be a generic approach for pure and substituted tetrahedrite synthesis, where the reaction was governed predominantly by thermodynamic control. 26 The solution state synthesis of tetrahedrite substituted with an additional transition metal (Zn, Ni, Co, Mn, and Fe) is further complicated by the cross-nucleation and/or formation of unwanted side products because of a narrow thermodynamic window, making it difficult to synthesize stoichiometric compounds with desired phases using readily available precursors.
Herein, we report a facile approach for the synthesis of compositionally tunable Cu 10 Zn 2 Sb 4 S 13 , Cu 10 Co 2 Sb 4 S 13 , and Cu 10 Ni 1.5 Sb 4 S 13 colloidal NCs. The NCs are produced by reacting metal salt precursors and tertiary dodecyl mercaptan (t-DDT) in the presence of 1-octadecene (ODE) and oleylamine (OLA). The coordinating solvent (OLA) facilitates the formation of an intermediate with the metal species and allows control of the NC size by selectively passivating the surface of the nucleated product. This circumvents the need for a separate reducing agent and ligands for the reaction. We observed that balancing the reactivity of Cu precursors with transition metals (Ni, Co, and Zn) is crucial to control the path of the reaction and to produce pure phase NCs with low polydispersity. Furthermore, the transport properties of these substituted nanostructures were measured in a temperature range from ambient to 490°C. While all of the produced complex materials exhibit very low thermal conductivities, Cu 10.5 Ni 1.5 Sb 4 S 13 further displays promising electrical conductivity, which makes it suitable for thermoelectric applications. Our results show that the transport properties of these NCs can be further enhanced by optimizing the level of substitution of the transition metal in the crystal structure of tetrahedrite (Cu 12−x Sb 4 S 13 ).  (25 mL) under an Ar atmosphere and connected to a Schlenk line via a condenser. The reaction mixture was evacuated for 40 min at 120°C to form a clear metal−ligand complex and to remove any moisture content. During heating, the color of the reaction mixture changed from dark blue to green at ≈80°C and finally to brownish orange at 120°C. Based on this color change, the dissolution of precursors in the solvent can be described as a reduction of Cu 2+ to Cu 1+ followed by the dissolution of Sb and Zn/Ni or Co. The reducing solvent oleylamine was used for the reduction of Cu 2+ to Cu 1+ in the reaction system. To produce a reducing environment, oleylamine forms a complex [Cu(OLA) 2 ] with the cation (Cu 2+ ), as was previously observed in the literature. 35,36 Although the copper cation in this complex is chelated, a dissociativeinterchange mechanism constantly exchanges the ligands with oleylamine from the solvent, leaving Cu 2+ available for the nucleophilic attack of the active sulfur source in the form of hydrogen sulfide. 36 After this, Ar was purged in the solution, the temperature was increased to 240°C, and 5 mmol t-DDT was swiftly injected, which turned the solution color into reddish brown in the case of Zn substitution and black for Ni and Co. The reaction was then allowed to proceed with continuous stirring for 15 min at 240°C for the growth of the nanocrystals. By removing the heating mantle, the reaction was stopped and the dark solution was quenched with 5 mL of anhydrous toluene after being allowed to cool down to 100°C. The obtained nanocrystals were isolated from the solution by centrifugation, and to effectively purify the nanocrystals, the mother liquor was divided into two 50 mL centrifuge tubes dispersed in 10 mL of hexane and centrifuged at 5000 rpm for 3 min. The remaining material was redispersed in hexane and acetone (3:1 v/v) and centrifuged for 5 min at 3000 rpm, following which the supernatant was discarded. After that, numerous precipitation and dispersion cycles employing chloroform/acetone/hexane (1:1:2 v/v) were used to further purify the semipure nanocrystals. The synthetic protocol for pure tetrahedrite (Cu 10 Sb 4 S 13 ) is provided in the Supporting Information.

Materials Characterization. 2.3.1. Electron Microscopy.
Transmission electron microscopy (TEM) and angular dark-field scanning transmission electron microscopy (STEM) were used to analyze the structure of the NCs on a JEOL JEM-2011F that was run at an accelerating voltage of 200 kV and mounted with a Gatan camera. Prior to imaging, samples were drop-casted on a nickel TEM grid. Using ImageJ software and counting >100 particles per sample, size statistics were calculated. On an FEI Titan Cubed Themis G2 300, aberration-corrected microscopy, high-resolution TEM (HRTEM) imaging, high-angle annular dark-field STEM (HAADF-STEM) imaging, and energy-dispersive X-ray spectroscopy (EDX) with elemental mapping were carried out.

X-Ray Diffraction (XRD) Analysis.
The XRD patterns of samples were acquired on an EMPYREAN with Cu Kα radiation and a one-dimensional Lynxeye detector. The sample was washed with isopropanol and acetone and then drop-casted on a glass slide for XRD analysis.

Raman Spectroscopy.
A 532 and 632.8 nm laser in an NT-MDT instrument mounted with NTEGRA spectra was used to gather the Raman data. The laser power of 2.5 mW and 20 s of integration times with 10 accumulations were used to get all spectra.

X-Ray Photoelectron Spectroscopy.
With the help of a Kratos Axis Ultra spectrometer, the NCs XPS data were collected. However, utilizing monochromated Al K radiation with an energy of 1486.6 eV at 20 eV, high-resolution spectra were recorded. A mixed Gaussian−Lorentzian function with a Shirley-type background subtraction was utilized for peak synthesis. Low-energy electrons were showered onto the samples to effectively neutralize the charge. Using the charge reference value of C 1s at 284.8 eV, binding energies (BE) were calculated. The sample was dropped onto a glass slide for drying under argon before being analyzed.

Inductively Coupled Plasma Mass Spectroscopy (ICP-MS).
For ICP-MS measurements, the samples were prepared by dissolving 1 mg in 2 mL of 1% HNO 3 at 80°C for 2 h. The solution was digested overnight at room temperature and diluted to 50, 40, and 10 ppm concentrations for the ICP-MS analysis.
2.3.6. Transport Properties. For transport property measurements, roughly 0.5 g of each NC composition was prepared. To remove the surface ligands, the NCs were washed thoroughly by several precipitation and dispersion steps until they remained insoluble. The washed NCs were vacuum-dried overnight in an oven at 70°C before the measurement of the thermoelectric properties. The cleaned and dried nanoparticles were annealed at 490°C and then hot- pressed into pellets. All of the measurements were carried out at temperatures below 490°C.

RESULTS
The synthesis protocol for the formation of the tetrahedritesubstituted NCs (Cu 1 0 Zn 2 Sb 4 S 1 3 , Cu 1 0 Co 2 Sb 4 S 1 3 , Cu 10 Ni 1.5 Sb 4 S 13 ), as shown in Figure 1a, involves the use of Cu(II) acetate, SbCl 3 , and metal salts (ZnCl 2 , Co(CH 3 COO) 2 · 4H 2 O and Ni(CH 3 COO) 2 ·4H 2 O) in the initial stage. A sulfur precursor (t-DDT) is subsequently introduced via separate injection at 240°C in the presence of 1-ODE as the noncoordinating solvent and oleylamine as the ligand.   Figure S1b,c) show that a good uniformity of NCs is achieved using this synthetic approach. The XRD patterns (Figure 3g) of all three nanostructures with Ni, Co, and Zn show patterns consistent with that of bulk tetrahedrite. However, the peak positions narrowly shifted to higher angles depending on the size of the substituted cation (Figure 3h). 37 Raman spectra ( Figure S3) of all of the synthesized NCs (Cu 10 Zn 2 Sb 4 S 13 , Cu 10 Co 2 Sb 4 S 13 , and Cu 10.5 Ni 1.5 Sb 4 S 13 ) show a strong peak at 357 cm −1 , which is a characteristic peak for tetrahedrite. 38 The vibrations of M− S bonds result in a strong Raman peak, while the observed shift in the frequencies of these peaks is due to the difference in the force constant for different incoming cations. Since Cu II −S bonds are transformed to M II −S bonds (M = Zn, Co, and Ni) during the formation of substituted tetrahedrite, the bond strength change causes a red shift in the Raman position (357 cm −1 ). HAADF-STEM ( Figure S4) with corresponding EDX elemental mapping shows a uniform distribution of all four elements in the Cu 10 Co 2 Sb 4 S 13 NCs. X-ray photoelectron spectroscopy (XPS) analysis was performed, as shown in Figure S5, to confirm the oxidation states of the constituent elements in the NCs. In the Cu XPS spectrum, an intense set of doublet peaks at 951.52 eV for 2p 1/2 and 931.75 eV for 2p 3/2 were observed. The two peaks are separated by 19 eV, confirming the presence of a Cu 1+ state. The absence of Cu II peaks also confirms that M II ions replaced the Cu II ion in the tetrahedrite (Cu 12−x I Cu II x Sb 4 S 13 ) structure. Inductively coupled plasma mass spectroscopy (ICP-MS) results show (Table S1) that the x value for Co and Zn in Cu 12−x M x Sb 4 S 13 is ∼2 (i.e., Cu 10 Zn 2 Sb 4 S 13 , Cu 10 Sb 4 Co 2 S 13 ), endorsing that the substituent bivalent ions replaced an equivalent amount of Cu II , while a value of 1.5 was observed for Ni (Cu 10 Ni 1.5 Sb 4 S 13 ).
We investigated the evolution of NCs during the formation of substituted tetrahedrite NCs (Cu 1 0 Zn 2 Sb 4 S 1 3 , Cu 10 Co 2 Sb 4 S 13 , and Cu 10.5 Ni 1.5 Sb 4 S 13 ) to further evaluate the formation mechanism of these NCs with different metal precursors. Figure 4 collates the results for the NC evolution within the Cu 10 Zn 2 Sb 4 S 13 crystal system. For the Cu 10 Zn 2 Sb 4 S 13 system, the Cu 1.8 S phase coexists with the quaternary (Cu 10 Zn 2 Sb 4 S 13 ) phase (Figure 4a) from 3 to 10 min upon the injection of the thiol source. After 5 min of injecting t-DDT, the peak intensity corresponding to Cu 1.8 S decreases and a small peak corresponding to ZnS emerges. The TEM analysis (Figure 4b) shows the presence of Cu 1.8 S hexagonal platelets at the initial stages after 5 min of reaction. Transformation of hollow particles to solid particles of average size 50 nm was observed for aliquots from 10 to 15 min. Two basic explanations have been put out to explain the mechanism of copper antimony sulfide-based nanocrystals: (i) interreaction theory and (ii) cation-exchange theory. According to the inter-reaction theory, the synthesis of copper-based ternary metal sulfides considers both the reaction between Cu 2 S and other binary metal sulfides in the reaction mixture and the reaction between chalcogen and the second metal. On the other hand, for the conventional cation-exchange theory, Cu x S preferentially forms in the early phases of the reaction based on the idea that copper ions are more reactive than those of other metals. In the cation-exchange reaction, the diffusion of foreign cations into the crystal structure is significantly influenced by the movement of the copper ion. Liang et al. reported Cu 12 Sb 4 S 13 synthesis by the reaction of preformed Cu 1.8 S and Sb 2 S 3 . 39 In the present report, we observe the presence of Cu 1.8 S at the initial stages with no evidence for the formation of Sb 2 S 3 , which suggested the sequential cationexchange process with in situ formed Cu 1.8 S for the formation of Cu 10 Zn 2 Sb 4 S 13 NCs instead of inter-reaction between binary sulfides. The morphology of the NCs changes from nanoplates to pyramid-shaped nanoparticles for Cu 10 Zn 2 Sb 4 S 13 NCs with  Figure S7). The cation-exchange reactions that have been carried out above 230°C for the synthesis of ternary metal chalcogenides with a reactive precursor of Zn would prefer heteroepitaxial formation of ZnS, according to earlier reports. 40 However, a decrease in the reactivity of the precursor will permit cationic diffusion in addition to shell formation. 26,41 In this study, we used ZnCl 2 as a Zn source, and according to the HSAB theory, borderline (Zn 2+ and Cl − ) acid and base make ZnCl 2 less reactive. This Zn precursor results in unequal diffusion between Cu 2+ and Zn 2+ on the similar S 2− anion frameworks resulting in the formation of hollow particles, as observed in the aliquot taken after 10 min, which further transformed to solid Cu 10 Zn 2 Sb 4 S 13 NCs after 15 min of reaction time with complete cation exchange between Cu 2+ and Zn 2+ . The evolution sequence of the Cu 10 Zn 2 Sb 4 S 13 NCs at different reaction times is schematically depicted in Figure 4c. Based on the above observations, the most likely growth mechanism is cation exchange. The growth process starts with the thermal decomposition of the Cu precursor to  Figure S8). The formation of quaternary Cu 10 Co 2 Sb 4 S 13 NCs ( Figure S9) was also observed within 5 min after the injection of the thiol source.

DISCUSSION
The findings compiled in Figure 5 demonstrate that phase control synthesis of tetrahedrite-substituted chalcogenides is attainable through a colloidal hot injection approach; however, it involves the suitable balancing of precursor reactivities. The hard and soft acid−base (HSAB) theory serves as a useful guide for predicting the reactivity of metal precursors. Based on the thiophilicity trends, Ni, Co, and Zn tend to form sulfur bonds more slowly compared to Cu. Therefore, Cu-(CH 3 COO) 2 , a Cu precursor of intermediate reactivity, was selected for combination with SbCl 3 . A series of experiments were conducted to investigate the reactivity of different transition metal (Ni, Co, and Zn) precursors to get purephase-substituted tetrahedrite NCs ( Figure S10). The Cu 10 Sb 4 Zn 2 S 13 NCs were synthesized by combining Zn in halide form, Cu in acetate, and Sb in halide form with thiol as an S source, while for the synthesis of Cu 10 Co 2 Sb 4 S 13 and Cu 10.5 Ni 1.5 Sb 4 S 13 NCs, hydrated acetates of Ni and Co were optimal. Strong interactions between chloride ions and Zn-ions make ZnCl 2 less reactive compared to Zn(CH 3 COO) 2 ·4H 2 O. Our observations show that in the presence of chloride, the overall rate of reaction between Cu precursors should be increased, while there was a decrease in the rate of reaction between the Zn precursor and S. This results in pure phase Cu 10 Sb 4 Zn 2 S 13 NCs. In contrast, the use of the chloride-based Ni precursor (NiCl 2 ) results in the growth of Cu x S byproducts ( Figure S10). It is known that Ni 2+ and Co 2+ are harder Lewis acids than Zn 2+ . 42 Therefore, to cope with the Cu precursor of  Mechanistically, the formation of multinary NCs can take place either directly from the solution containing a mixture of precursors or through a solid-state reaction. 7,39 According to the HSAB theory, the metal precursors will react with the S precursor (a soft Lewis base) in the order of Cu 2+ > Zn 2+ > Sb 3+ . However, the presence of coordinating ligands in the reaction mixture and their different coordination with different metal precursors adds an extra layer of complexity. 43 The reported literature based on mechanistic insight for the synthesis of the ternary Cu−Sb−S system depicts that the in situ formed Cu x S seed is responsible for the growth of Cu− Sb−S NCs. 44 For all three substituted tetrahedrite NCs (Cu 10 Zn 2 Sb 4 S 13 , Cu 10 Co 2 Sb 4 S 13 , and Cu 10.5 Ni 1.5 Sb 4 S 13 ), Cu x S was observed at the initial stages, suggesting that the formation of quaternary NCs followed a successive cation-exchange mechanism between Cu 2+ and foreign cations (Sb 3+ and Zn 2+ ). Based on the observations discussed in the previous section ( Figure 4) and the results described above (Figure 5), we can relate the growth mechanism with the reactivity of transition metal precursors. In the case of Cu 10 Zn 2 Sb 4 S 13 , after the formation of (Cu + ) 10 (Cu 2+ ) 2 Sb 4 S 13 , the less reactive chloridebased Zn precursor results in unequal diffusion on the same S 2− anion frameworks between Cu and Zn, resulting in the formation of hollow particles for an aliquot taken after 10 min, which further transformed to solid Cu 10 Zn 2 Sb 4 S 13 NCs after 15 min of reaction with complete cation exchange between Cu 2+ and Zn 2+ . On the other hand, for Cu 10 Co 2 Sb 4 S 13 and Cu 10.5 Ni 1.5 Sb 4 S 13 , the diffusion of Ni and Co with more reactive acetate-based Co and Ni precursors is so fast that it results in quaternary composition within 5 min of reaction. These findings suggest that the metal-to-ligand complex that formed in the case of Cu 10 Co 2 Sb 4 S 13 and Cu 10.5 Ni 1.5 Sb 4 S 13 is not strong compared to Cu 10 Zn 2 Sb 4 S 13 , which results in the evolution of cubic phase NCs after 5 min because of faster ionic diffusion of Ni and Co compared to Zn for Cu 10 Zn 2 Sb 4 S 13 .

TRANSPORT PROPERTIES
The transport properties of pure (Cu 12 Sb 4 S 13 ) and substituted tetrahedrites (Cu 10 Zn 2 Sb 4 S 13 , Cu 10 Co 2 Sb 4 S 13 , and Cu 10.5 Sb 4 Ni 1.5 S 13 ) were investigated in the temperature range of 300−700 K. Figure 6 shows the electrical conductivity (σ), Seebeck coefficient (S), thermal conductivity (κ), and overall thermoelectric figure of merit (ZT = S 2 σT/κ) for Cu 12 Sb 4 S 13 , Cu 10 Co 2 Sb 4 S 13 , and Cu 10.5 Ni 1.5 Sb 4 S 13 NCs. The transport properties show an increase in electrical conductivity and power factor with a decrease in thermal conductivity upon substitution of the transition metal (Co and Ni) ( Figure 6). While all of the synthesized crystal phases display outstanding low thermal conductivity, the Cu 10.5 Sb 4 Ni 1.5 S 13 system shows the most enhanced electrical conductivity compared to Cu 10 Zn 2 Sb 4 S 13 and Cu 10 Co 2 Sb 4 S 13 . 45 The optical bandgaps were reduced relative to the pure tetrahedrite for the synthesized material (Figures S15d and S16 and Table S2).
The hybridization of Cu 3d and S 3p orbitals results in the formation of pure tetrahedrite (Cu + ) 10 (Cu 2+ ) 2 Sb 4 S 13 . The valence bands of S and Sb p orbitals are separated from the conduction bands in pure tetrahedrite by a clearly defined energy gap. The tetrahedrite material generally behaves as a degenerated p-type semiconductor. This heavy p-type doping is associated with the existence of an extra S 2− ion and two unfilled holes, which is maintained by covalent interactions with the s and d orbitals of neighboring Cu + ions on the 12e sites. The electric resistivity of pellets by substituting Cu with the d 10 cation (Zn 2+ ) is higher (Table S2). Previous reports and DFT calculations have demonstrated that two Zn atoms are substituted for Cu, and as a result, the holes in the valence band are filled with the extra 4s electrons, and the material turns insulating. 45 Similar behavior is consistent with the results observed here for Cu 12−x Zn x Sb 4 S 13 NCs with x = 2 in the tetrahedrite structure (Cu 12 Sb 4 S 13 ), suggesting that the material is an insulator. In contrast, Ni-containing materials show the highest electrical conductivity and lowest Seebeck coefficient, which clearly indicates a large increase in the charge carrier concentration. The electrical conductivity of Cu 10.5 Ni 1.5 Sb 4 S 13 NCs (Figure 6a) does not show a clear evolution with temperature as two effects counteract the thermal excitation of the additional charge carrier and their lattice scattering with increasing temperature. The thermal excitation of electrons in the impurity state from the valence band is what causes the slight reduction in electrical conductivity above 400°C. Ni-doping due to the hybridization of Cu 3d states and S 3p states with the valence band of Ni 3d states produces spin splitting, which results in higher electrical conductivity of the Ni-substituted NCs. Thus, thermal excitation of the carriers becomes easier as a result of a narrower bandgap. 37 The optical data and Tauc plot of the assynthesized Cu 10.5 Ni 1.5 Sb 4 S 13 NCs are provided in Figure  S16c,d.
The Seebeck coefficient (S) for Cu 10 Sb 4 S 13 , Cu 10 Co 2 Sb 4 S 13 , and Cu 10.5 Ni 1.5 Sb 4 S 13 NCs (Figure 6b) is positive over the whole temperature range, indicating a p-type conductivity where holes make up the majority of the charge carriers. The mean heat capacity (C p ) used in this study to calculate the thermal conductivity was 0.45 J g −1 K −1 . 46 The synthesized materials display remarkably low thermal conductivity ( Figure  6c), well below 1 W m −1 K −1 , which is associated with the crystal structure, complex composition, and the large density of grain boundaries. The decrease in the thermal conductivity of Cu 10 Co 2 Sb 4 S 13 and Cu 10.5 Ni 1.5 Sb 4 S 13 with the increase in temperature can be explained on the basis of phonon scattering enhancement. 46 Overall, the ZT value (Figure 6d) of all substituted NCs increases with the increase in temperature. The transport properties for tetrahedrite-based samples vary widely depending on factors such as the synthesis and sintering conditions, dopant, and doping levels. 28 Thus, the NCs synthesized using the hot injection reaction protocol with different dopants (Zn, Ni, and Co) show different thermoelectric properties depending on the level of the dopant (x = 1.5−2), highlighting the role of the dopant and doping level on the thermoelectric figures.

CONCLUSIONS
In summary, we have shown that tetrahedrite-substituted NCs can be formed by a hot injection process that requires less energy and time compared to traditional solid-state methods. This research focused on a generalized synthesis approach for pure-phase pyramid-shaped NCs by optimizing the reactivity of precursors with different reaction parameters. The evolution of pure phases for the bottom-up production of substituted tetrahedrite has been identified by examining the progress of the reactions over time. The key intermediate identified within the growth process is Cu 1.8 S and is observed consistently for all of the three substituted NCs. The synthesis approach is simple, yielding exclusive quaternary NCs of controlled shape and size, and is sufficiently versatile to be exploited for the future synthesis of a large variety of I−II−V−VI-based NCs. The transport properties of these samples showed that the Nisubstituted NCs with Cu 10.5 Sb 4 Ni 1.5 S 13 composition exhibit the most promising transport properties compared to that of Zn or Co. These findings suggest that by optimizing the level of substitution of the transition metal in the crystal structure of tetrahedrite (Cu 12−x Sb 4 S 13 ), the thermoelectric performance of these NCs can be further tuned.
Additional data of size distribution histograms, Rietveld refinement, Raman, and XPS, along with UV−vis spectra of the synthesized nanocrystals (PDF) ■ ACKNOWLEDGMENTS